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(11) | EP 3 299 348 A1 |
| (12) | EUROPEAN PATENT APPLICATION |
| published in accordance with Art. 153(4) EPC |
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| (54) | BORON-FREE GLASS FIBER COMPOSITION, AND GLASS FIBER AND COMPOSITE MATERIAL THEREOF |
(57) A Boron-free glass fiber composition, and a glass fiber and a composite material
thereof. The glass fiber composition comprises the following components in percentage
by weight: 58% to 60.4% of SiO2, 14% to 16.5% of Al2O3, 14.1% to 16.5% of CaO, 6% to 8.2% of MgO, 0.01% to 0.5% of Li2O, less than 1.15% of Na2O+K2O, K2O being higher than 0.5%, less than 1.5% of TiO2, and less than 1% of Fe2O3, the ratio in percentage by weight C1=CaO/MgO being greater than 2 and smaller than
or equal to 2.4. The composition can remarkably reduce the surface tension of glass,
improve the mechanical strength and the chemical resistance stability of the glass
fiber, effectively suppress the crystallization tendency of glass, reduce the liquidus
temperature of glass, and is particularly suitable for producing high-performance
glass fiber having a low bubble rate.
FIELD OF THE INVENTION
[0001] The invention relates to boron-free glass fiber compositions, in particular, to high performance boron-free glass fiber compositions that can be used as a reinforcing base material for advanced composites, and to the glass fiber and composite material therefrom.
BACKGROUND OF THE INVENTION
[0002] Glass fiber is an inorganic fiber material that can be used to reinforce resins to produce composite materials with good performance. As a reinforcing base material for advanced composite materials, high-performance glass fibers were originally used mainly in the national defense industry, such as aeronautic, aerospace and military industry. With the progress of science and technology and the development of economy, high-performance glass fibers have been widely used in civil and industrial fields such as motors, wind blades, pressure vessels, offshore oil pipes, sports apparatus and auto industry.
[0003] Since Owens Corning (hereinafter referred to as OC) of the US developed S-2 glass fiber, different countries have competed in developing high-performance glass fibers with various compositions, e.g. R glass fiber developed by Saint-Gobain of France, HiPer-tex glass fiber developed by OC of US and high-strength glass fiber 2# developed by Nanjing Fiberglass Research & Design Institute Co. Ltd of China. The original high-performance glass compositions were based on an MgO-Al2O3-SiO2 system and a typical composition was the S-2 glass developed by OC. However, the production of S-2 glass is excessively difficult, as its forming temperature is up to about 1571°C and its liquidus temperature is up to 1470°C and therefore, it is difficult to realize large-scale industrial production. Then OC gave up the production of S-2 glass fiber and assigned the patent to AGY company which has been devoted to the small-scale production of S glass fiber and its improved products.
[0004] Thereafter, in order to decrease the melting temperature and forming temperature of the glass to better satisfy the needs of large-scale tank furnace production, large foreign companies successively developed high-performance glasses based on an MgO-CaO-Al2O3-SiO2 system. Typical compositions were R glass developed by Saint-Gobain of France and HiPer-tex glass developed by OC of the US, which were a trade-off for production scale by sacrificing some of the glass properties. However, as these designed solutions were too conservative, especially the content of Al2O3 was kept more than 20%, preferably 25%, the production of glass remained highly difficult. Although small-scale tank furnace production was achieved, the production efficiency was low and the cost-performance ratio of the products was not high. Then OC gave up the production of HiPer-tex glass fiber and assigned the patent of HiPer-tex glass fiber to 3B company of Europe. Around 2007, OCV Company was established under the combination of OC and Saint-Gobain, and the core technologies of R glass fiber were assigned to OCV Company. The ratio of Ca/Mg in the traditional R glass is too low, which will cause problems such as fiberizing difficulty, high risk of crystallization, high surface tension and fining difficulty of molten glass; the forming temperature is up to about 1410°C and the liquidus temperature up to 1330 °C. All these have caused difficulty in attenuating glass fiber and consequently in realizing large-scale industrial production.
[0005] In addition, PPG Industries has disclosed another type of R glass fiber. Its mechanical performance is slightly lower than that of the traditional R glass fiber, but the melting and forming performance are significantly superior to those of the traditional R glass. However, this type of R glass has a high risk of devitrification because the ratios of Si/Ca and Ca/Mg are not reasonably designed. Meanwhile, since too much Li2O is introduced, not only the chemical stability of the glass is affected, but also its raw material cost gets significantly higher. Therefore it is also not suitable for large-scale industrial production.
[0006] The High-strength 2# glass fiber mainly comprises SiO2, Al2O3 and MgO, and certain amounts of Li2O, B2O3, CeO2 and Fe2O3 are also introduced. It also has high strength and high modulus and its forming temperature is only about 1245°C and its liquidus temperature is 1320°C. Both temperatures are much lower than those of S glass fiber. However, since its forming temperature is lower than its liquidus temperature, which is unfavorable for the control of glass fiber attenuation, the forming temperature has to be increased and specially-shaped tips of bushing have to be used to prevent a glass crystallization phenomenon from occurring in the fiber drawing process. This causes difficulty in temperature control and also makes it difficult to realize large-scale industrial production.
[0007] In summary, we have found that, various kinds of high-performance glass fibers generally face production problems such as high liquidus temperature, high risk of devitrification, high forming temperature, high surface tension and fining difficulty of molten glass. The liquidus temperature of the mainstream E-glass is generally less than 1200°C, and its forming temperature is lower than 1300°C, while the above-mentioned high-performance glass fibers generally have liquidus temperatures higher than 1300°C and forming temperatures higher than 1350°C, which can easily cause glass crystallization phenomenon, uneven viscosity and poor fining, thereby greatly reducing the production efficiency, product quality and the service life of refractory materials and platinum bushings.
SUMMARY OF THE INVENTION
[0008] The present invention aims to provide a boron-free glass fiber composition that can solve the aforesaid problems.
[0009] According to one aspect of the present invention, the glass fiber composition is provided comprising the following components expressed as percentage by weight:
| SiO2 | 58-60.4% |
| Al2O3 | 14-16.5% |
| CaO | 14.1-16.5% |
| MgO | 6-8.2% |
| Li2O | 0.01-0.4% |
| Na2O+K2O | less than 1.15% |
| K2O | greater than 0.5% |
| TiO2 | less than 1.5% |
| Fe2O3 | less than 1% |
[0010] Wherein, the range of the weight percentage ratio C2= K2O/Na2O is greater than 1 and less than or equal to 6.
[0011] Wherein, the preferred range of the weight percentage ratio C1=CaO/MgO is greater than 2 and less than or equal to 2.3.
[0013] According to another aspect of this invention, a glass fiber produced with said glass fiber composition is provided.
[0014] According to yet another aspect of this invention, a composite material incorporating said glass fiber is provided.
[0015] According to the composition of this invention, a high performance boron-free glass fiber composition is provided by introducing appropriate amounts of K2O and Li2O, reasonably designing the ranges of contents of CaO, MgO, K2O and Li2O respectively, strictly controlling the ranges of the ratios of CaO/MgO and K2O/Na2O, making full use of the ternary mixed alkali effect of K2O, Na2O and Li2O, and selectively introducing a small amount of ZrO2 and HfO2.
[0016] Specifically, the glass fiber composition according to the present invention comprises the following components expressed as percentage by weight:
| SiO2 | 58-60.4% |
| Al2O3 | 14-16.5% |
| CaO | 14.1-16.5% |
| MgO | 6-8.2% |
| Li2O | 0.01-0.4% |
| Na2O+K2O | less than 1.15% |
| K2O | greater than 0.5% |
| TiO2 | less than 1.5% |
| Fe2O3 | less than 1% |
[0017] The effect and content of each component in said glass fiber composition is described as follows:
SiO2 is a main oxide forming the glass network and has the effect of stabilizing all the components. In the glass fiber composition of the present invention, the restricted content range of SiO2 is 58-60.4% by weight. In order to ensure the high mechanical properties, and meanwhile not increase the fining difficulty of glass, the content range of SiO2 in the glass fiber composition of this invention is specially kept relatively low. Preferably, the SiO2 content range can be 58.5-60.4% by weight.
Al2O3 is another oxide forming the glass network. When combined with SiO2, it can have a substantive effect on the mechanical properties of the glass and a significant effect on preventing glass phase separation and on water resistance. The restricted content range of Al2O3 in the glass fiber composition of this invention is 14-16.5% by weight. The high mechanical properties, especially modulus, cannot be obtained if Al2O3 content is too low; Al2O3 content being too high will cause the glass viscosity to be excessively high, thereby resulting in melting and fining issues. Preferably, the Al2O3 content can be 14.5-16.5% by weight.
CaO is an important glass network modifier, it has particular effects in reducing glass viscosity at high temperature, controlling the crystallization and the hardening rate of molten glass, but the CaO content being too high will cause higher crystallization tendency of glass, thereby resulting in the crystallization of anorthite (CaAl2Si2O8) and wollastonite (CaSiO3) from the glass melt. The restricted content range of CaO in the glass fiber composition of this invention is 14.1-16.5% by weight. Preferably, the CaO content can be 14.1-16.1% by weight.
MgO has an effect similar to that of CaO, and yet the Mg2+ has higher field strength and plays a significant role in increasing the modulus of glass. However, the MgO content being too high will increase the tendency and rate of the glass crystallization, thus causing the risk of diopside (CaMgSi2O6) crystallization, which is more violent compared with that caused by CaO. The restricted content range of MgO in the glass fiber composition of this invention is 6-8.2% by weight. Preferably, the MgO content can be 6-8% by weight.
[0018] Additionally, the crystalline phase after the crystallization of high-performance glasses based on an MgO-CaO-Al2O3-SiO2 system mainly comprises diopside (CaMgSi2O6), anorthite (CaAl2Si2O8) and wollastonite (CaSiO3). In order to effectively inhibit the growth of these crystals, reduce the upper limit temperature for glass crystallization (liquidus temperature) and reduce the crystallization tendency of glass, in the glass fiber composition of the present invention, the weight percentage ratio C1=CaO/MgO is greater than 2 and less than or equal to 2.4. By controlling the range of molar ratio of Ca2+/Mg2+ to be about 1.42-1.72, the crystal growth of anorthite could balance against that of diopside in the crystallization process of glass, which helps to reduce the two crystals crystallization rate and the crystal grain integrity, simultaneously inhibit the crystallization tendency of the two crystals and reduce liquidus temperature. This is because the above-mentioned ratio can take advantage of the high field strength of Mg2+ while ensuring a sufficient supply of Ca2+ ions during the crystallization of glass, and make full use of the competition between Mg2+ and Ca2+ ions in grabbing the anion groups in the glass. Obviously, the ratio of CaO/MgO being too low will cause too much content of Mg2+, and aggravate the crystallization of diopside; the weight percent ratio of CaO/MgO being too high will cause too much content of Ca2+, and aggravate the crystallization of anorthite, or even cause the wollastonite crystals to form, thus greatly affecting the competitive growth balance of crystals. Preferably, the range of the weight percentage ratio C1=CaO/MgO can be greater than 2 and less than or equal to 2.3. More preferably, the range of the weight percentage ratio C1=CaO/MgO can be greater than 2 and less than or equal to 2.14. The technical effects can be unexpectedly achieved as compared with those with traditional high-performance glasses. Additionally, the mechanical strength of glass is better when the content of CaO is kept relatively high due to the high bond energy of Ca-O, which also has a significant effect on the accumulation of glass structure.
[0019] Both K2O and Na2O are good fluxing agents that can reduce glass viscosity. The inventors have found that, replacing Na2O with K2O while keeping the total amount of alkali metal oxides unchanged can reduce the crystallization tendency of glass, improve the fiberizing performance, and also remarkably reduce the surface tension of molten glass and improve the fining performance; and help to improve the mechanical strength of glass. In the glass fiber composition of this invention, the restricted range of the total content of Na2O and K2O is less than 1.15% by weight, the restricted content range of K2O is greater than 0.5% by weight, and the range of the weight percentage ratio C2 = K2O/Na2O can be further restricted to be greater than 1 and less than or equal to 6. Preferably, the range of the weight percentage ratio C2 = K2O/Na2O can be 1.2-5.
[0020] Li2O can not only reduce the glass viscosity dramatically to improve melting performance, but also obviously help to improve mechanical properties, compared with Na2O and K2O. In addition, a small amount of Li2O can provide considerable free oxygen, thereby promoting more aluminum ions to form tetrahedral coordination that would help strengthen the glass network and further reduce crystallization tendency of glass. But the added amount of Li2O should not be too high, as the content of Li+ being too high will have a significant effect in disrupting the glass network, affect the stability of glass structure, and thus increase the crystallization tendency of glass. Therefore, in the glass fiber composition of the present invention, the restricted range of the content of Li2O is 0.01-0.4% by weight. The inventors have found that the technical effects remain excellent even when the content of Li2O is kept relatively low, such as greater than or equal to 0.01% and less than 0.1 % by weight.
[0021] TiO2 can not only reduce the glass viscosity at high temperature, but also has a certain fluxing effect. However, since titanium ions have coloring effects, which will become particularly significant especially when the TiO2 content is greater than 1.5% by weight, thus affecting the appearance of fiberglass products to a certain extent. Therefore, in the glass fiber composition of this invention, the restricted range of the content of TiO2 is less than 1.5% by weight.
[0022] The introduction of Fe2O3 facilitates the melting of glass and can also improve the crystallization properties of glass. However, since ferric ions and ferrous ions have coloring effects, the introduced amount should be limited. Therefore, in the glass fiber composition of the present invention, the restricted range of the content of Fe2O3 is less than 1% by weight.
[0023] Additionally, a small amount of ZrO2 and HfO2 can be selectively introduced, which can further improve mechanical properties and thermal stability of the glass. Considering ZrO2 and HfO2 would increase glass viscosity, the added amounts of them should not be too high. Therefore, in the glass fiber composition of the present invention, the restricted range of the total content of ZrO2 and HfO2 is 0.01-2% by weight.
[0024] In addition to aforementioned components, small amounts of impurities may be present in the glass composition according to the present invention, and the total weight percentage of the impurities is less than or equal to 1%.
[0025] In the glass fiber composition of the present invention, the beneficial effects produced by the aforementioned selected ranges of the components will be explained through the specific experimental data provided below.
[0026] The following are embodiments of preferred content ranges of the components comprised in the glass fiber composition according to the present invention.
Preferred embodiment 1
[0027] The glass fiber composition according to the present invention comprises the following components expressed as percentage by weight:
| SiO2 | 58.5-60.4% |
| Al2O3 | 14.5-16.5% |
| CaO | 14.1-16.1% |
| MgO | 6-8% |
| Li2O | 0.01-0.4% |
| Na2O+K2O | less than 1.15% |
| K2O | greater than 0.5% |
| TiO2 | less than 1.5% |
| Fe2O3 | less than 1% |
Preferred embodiment 2
[0028] The glass fiber composition according to the present invention comprises the following components expressed as percentage by weight:
| SiO2 | 58.5-60.4% |
| Al2O3 | 14.5-16.5% |
| CaO | 14.1-16.1% |
| MgO | 6-8% |
| Li2O | 0.01-0.4% |
| Na2O+K2O | less than 1.15% |
| K2O | greater than 0.5% |
| TiO2 | less than 1.5% |
| Fe2O3 | less than 1% |
Preferred embodiment 3
[0029] The glass fiber composition according to the present invention comprises the following components expressed as percentage by weight:
| SiO2 | 58.5-60.4% |
| Al2O3 | 14.5-16.5% |
| CaO | 14.1-16.1% |
| MgO | 6-8% |
| Li2O | greater than or equal to 0.01 % and less than 0.1 % |
| Na2O+K2O | less than 1.15% |
| K2O | greater than 0.5% |
| TiO2 | less than 1.5% |
| Fe2O3 | less than 1% |
[0030] The present invention provides a boron-free glass fiber composition, glass fiber and composite material therefrom. The composition can not only keep the forming temperature relatively low, but also solve the problems in the production of high-performance glass fiber, such as high liquidus temperature, high crystallization rate, high surface tension, fining difficulty, and the difficulty in efficient and large-scale production. The composition can significantly reduce liquidus temperature and surface tension of molten glass, and reduce crystallization tendency of glass and the amount of bubbles under the same conditions. Meanwhile, the glass fiber made therefrom possesses favorable mechanical strength.
DETAILED DESCRIPTION OF THE INVENTION
[0031] In order to better clarify the purposes, technical solutions and advantages of the examples of the present invention, the technical solutions in the examples of the present invention are clearly and completely described below combined with the drawings in the examples. Obviously, the examples described herein are just part of the examples of the present invention and are not all the examples. All other exemplary embodiments obtained by one skilled in the art on the basis of the examples in the present invention without performing creative work shall all fall into the scope of protection of the present invention. What needs to be made clear is that, as long as there is no conflict, the examples and the features of examples in the present application can be arbitrarily combined with each other.
[0032] The basic concept of the present invention is that, the glass fiber composition comprises the following components expressed as percentage by weight: SiO2 58-60.4%, Al2O3 14-16.5%, CaO 14.1-16.5%, MgO 6-8.2%, Li2O 0.01-0.5%, Na2O+K2O less than 1.15%, K2O greater than 0.5%, TiO2 less than 1.5% and Fe2O3 less than 1%, wherein the range of the weight percentage ratio C1 = CaO/MgO is greater than 2 and less than or equal to 2.4. In addition, the range of the weight percentage ratio C2 = K2O/Na2O can be further restricted to be greater than 1 and less than or equal to 6.
[0033] The specific content values of SiO2, Al2O3, CaO, MgO, Na2O, K2O, Fe2O3, Li2O, and TiO2 in the glass fiber composition of the present invention are selected to be used in the examples, which are compared with the properties of traditional E and R glasses and improved R glass in terms of the following six property parameters:
- (1) Forming temperature, the temperature at which the glass melt has a viscosity of 103 poise.
- (2) Liquidus temperature, the temperature at which the crystal nucleuses begin to form when the glass melt cools off, i.e., the upper limit temperature for glass crystallization.
- (3) ΔT value, which is the temperature differential between the forming temperature and the liquidus temperature and indicates the temperature range at which fiber drawing can be performed.
- (4) Crystallization peak temperature, the temperature of the strongest crystallization peak in the DTA (Differential Thermal Analysis) test. Generally, the higher the temperature is, the more energy that the crystal nucleuses need to grow up, and the smaller crystallization tendency of the glass is.
- (5) Filament strength, the tensile strength that a filament of glass fiber strand can withstand.
- (6) Amount of bubbles, to be determined approximately in a procedure set out as follows: Use specific moulds to compress the batch materials in each example into samples of same dimension, which will then be placed on the sample platform of a heating microscope. Heat the glass samples according to standard procedures up to the pre-set spatial temperature 1500° C, and then the glass sample is cooled to the ambient temperature without heat preservation. Finally, each of the glass samples is examined under a polarizing microscope to determine the amount of bubbles in the samples. Wherein, the amount of bubbles is identified according to a specific amplification of the microscope.
[0034] The aforementioned six parameters and the methods of measuring them are well-known to one skilled in the art. Therefore, the aforementioned parameters can be effectively used to explain the properties of the glass fiber composition of the present invention.
[0035] The specific procedures for the experiments are as follows: Each component can be acquired from the appropriate raw materials; the raw materials are mixed in the appropriate proportions so that each component reaches the final expected weight percentage; the mixed batch is melted and clarified; then the molten glass is drawn out through the tips of the bushings, thereby forming the glass fiber; the glass fiber is attenuated onto the rotary collet of a winder to form cakes or packages. Of course, conventional methods can be used to deep process these glass fibers to meet the expected requirements.
[0036] The exemplary embodiments of the glass fiber composition according to the present invention are given below.
Example 1
[0037]
| SiO2 | 59.8% |
| Al2O3 | 15.4% |
| CaO | 15.5% |
| MgO | 7.3% |
| Li2O | 0.09% |
| Na2O | 0.33% |
| K2O | 0.49% |
| Fe2O3 | 0.42% |
| TiO2 | 0.47% |
[0038] In Example 1, the measured values of the six parameters are respectively:
| Forming temperature | 1277°C |
| Liquidus temperature | 1197°C |
| ΔT | 80°C |
| Crystallization peak temperature | 1026°C |
| Filament strength | 4140MPa |
| Amount of bubbles | 6 |
Example 2
[0039]
| SiO2 | 60.0% |
| Al2O3 | 15.2% |
| CaO | 15.4% |
| MgO | 7.2% |
| Li2O | 0.25% |
| Na2O | 0.22% |
| K2O | 0.75% |
| Fe2O3 | 0.43% |
| TiO2 | 0.35% |
[0040] In Example 2, the measured values of the six parameters are respectively:
| Forming temperature | 1276°C |
| Liquidus temperature | 1195°C |
| ΔT | 81°C |
| Crystallization peak temperature | 1034°C |
| Filament strength | 4149MPa |
| Amount of bubbles | 4 |
Example 3
[0041]
| SiO2 | 59.1% |
| Al2O3 | 15.5% |
| CaO | 15.6% |
| MgO | 7.1% |
| Li2O | 0.25% |
| Na2O | 0.21% |
| K2O | 0.85% |
| Fe2O3 | 0.41% |
| TiO2 | 0.38% |
| ZrO2+HfO2 | 0.4% |
[0042] In Example 3, the measured values of the six parameters are respectively:
| Forming temperature | 1276°C |
| Liquidus temperature | 1196°C |
| ΔT | 80°C |
| Crystallization peak temperature | 1030°C |
| Filament strength | 4143MPa |
| Amount of bubbles | 6 |
Example 4
[0043]
| SiO2 | 58.5% |
| Al2O3 | 14% |
| CaO | 16.1% |
| MgO | 8% |
| Li2O | 0.39% |
| Na2O+K2O | 1.14% |
| K2O | 0.95% |
| TiO2 | 1% |
| Fe2O3 | 0.87% |
[0044] In Example 4, the measured values of the six parameters are respectively:
| Forming temperature | 1266°C |
| Liquidus temperature | 1190°C |
| ΔT | 76°C |
| Crystallization peak temperature | 1042°C |
| Filament strength | 4195MPa |
| Amount of bubbles | 3 |
Example 5
[0045]
| SiO2 | 59% |
| Al2O3 | 14% |
| CaO | 16.5% |
| MgO | 8.2% |
| Li2O | 0.39% |
| Na2O+K2O | 1.14% |
| K2O | 0.95% |
| TiO2 | 0.5% |
| Fe2O3 | 0.37% |
[0046] In Example 5, the measured values of the six parameters are respectively:
| Forming temperature | 1268°C |
| Liquidus temperature | 1192°C |
| ΔT | 76°C |
| Crystallization peak temperature | 1038°C |
| Filament strength | 4123MPa |
| Amount of bubbles | 5 |
Example 6
[0047]
| SiO2 | 58% |
| Al2O3 | 16.5% |
| CaO | 16.5% |
| MgO | 6.875% |
| Li2O | 0.4% |
| Na2O+K2O | 0.725% |
| K2O | 0.5% |
| TiO2 | 0.5% |
| Fe2O3 | 0.5% |
[0048] In Example 6, the measured values of the six parameters are respectively:
| Forming temperature | 1271°C |
| Liquidus temperature | 1194°C |
| ΔT | 77°C |
| Crystallization peak temperature | 1035°C |
| Filament strength | 4135MPa |
| Amount of bubbles | 6 |
Example 7
[0049]
| SiO2 | 60.4% |
| Al2O3 | 16% |
| CaO | 14.1% |
| MgO | 7% |
| Li2O | 0.21% |
| Na2O+K2O | 1.105% |
| K2O | 0.9% |
| TiO2 | 0.285% |
| Fe2O3 | 0.9% |
[0050] In Example 7, the measured values of the six parameters are respectively:
| Forming temperature | 1275°C |
| Liquidus temperature | 1194°C |
| ΔT | 81°C |
| Crystallization peak temperature | 1036°C |
| Filament strength | 4201MPa |
| Amount of bubbles | 4 |
Example 8
[0051]
| SiO2 | 60.3% |
| Al2O3 | 14.5% |
| CaO | 16.1% |
| MgO | 7% |
| Li2O | 0.39% |
| Na2O+K2O | 1.1% |
| K2O | 0.6% |
| TiO2 | 1.21% |
| Fe2O3 | 0.4% |
[0052] In Example 8, the measured values of the six parameters are respectively:
| Forming temperature | 1275°C |
| Liquidus temperature | 1195°C |
| ΔT | 80°C |
| Crystallization peak temperature | 1035°C |
| Filament strength | 4144MPa |
| Amount of bubbles | 5 |
Example 9
[0053]
| SiO2 | 59.36% |
| Al2O3 | 14.9% |
| CaO | 14.4% |
| MgO | 6% |
| Li2O | 0.3% |
| Na2O+K2O | 1.14% |
| K2O | 0.6% |
| TiO2 | 0.4% |
| Fe2O3 | 0.9% |
| ZrO2+HfO2 | 2% |
[0054] In Example 9, the measured values of the six parameters are respectively:
| Forming temperature | 1278°C |
| Liquidus temperature | 1196°C |
| ΔT | 82°C |
| Crystallization peak temperature | 1031°C |
| Filament strength | 4183MPa |
| Amount of bubbles | 9 |
Example 10
[0055]
| SiO2 | 59.36% |
| Al2O3 | 16.5% |
| CaO | 14.4% |
| MgO | 6% |
| Li2O | 0.3% |
| Na2O+K2O | 1.14% |
| K2O | 0.6% |
| TiO2 | 1.39% |
| Fe2O3 | 0.9% |
| ZrO2+HfO2 | 0.01% |
[0056] In Example 9, the measured values of the six parameters are respectively:
| Forming temperature | 1276°C |
| Liquidus temperature | 1196°C |
| ΔT | 80°C |
| Crystallization peak temperature | 1030°C |
| Filament strength | 4192MPa |
| Amount of bubbles | 5 |
[0057] Comparisons of the property parameters of the aforementioned examples and other examples of the glass fiber composition of the present invention with those of the traditional E glass, traditional R glass and improved R glass are further made below by way of tables, wherein the component contents of the glass fiber composition are expressed as weight percentage. What needs to be made clear is that the total amount of the components in the examples is slightly less than 100%, and it should be understood that the remaining amount is trace impurities or a small amount of components which cannot be analyzed.
Table 1
| A1 | A2 | A3 | A4 | A5 | A6 | A7 | ||
| Component | SiO2 | 59.6 | 59.0 | 58.7 | 60.4 | 60.0 | 59.8 | 59.1 |
| Al2O3 | 15.5 | 14.8 | 15.6 | 15.9 | 16.5 | 15.4 | 15.5 | |
| CaO | 15.6 | 16.5 | 16.0 | 15.2 | 14.1 | 15.5 | 15.6 | |
| MgO | 7.4 | 8.0 | 7.7 | 6.4 | 7.0 | 7.3 | 7.1 | |
| Na2O | 0.21 | 0.29 | 0.25 | 0.21 | 0.28 | 0.33 | 0.21 | |
| K2O | 0.58 | 0.51 | 0.63 | 0.61 | 0.65 | 0.49 | 0.85 | |
| Li2O | 0.15 | 0.01 | 0.15 | 0.30 | 0.40 | 0.09 | 0.25 | |
| Fe2O3 | 0.41 | 0.44 | 0.41 | 0.41 | 0.41 | 0.42 | 0.41 | |
| TiO2 | 0.33 | 0.33 | 0.36 | 0.37 | 0.46 | 0.47 | 0.38 | |
| ZrO2+HfO2 | - | - | - | - | - | - | 0.4 | |
| Ratio | C1 | 2.11 | 2.07 | 2.08 | 2.38 | 2.02 | 2.13 | 2.20 |
| C2 | 2.77 | 1.76 | 2.52 | 2.91 | 2.33 | 1.49 | 4.05 | |
| Parameter | Forming temperature/°C | 1277 | 1274 | 1276 | 1277 | 1277 | 1277 | 1276 |
| Liquidus temperature/°C | 1196 | 1194 | 1193 | 1201 | 1195 | 1197 | 1196 | |
| ΔT/°C | 81 | 80 | 83 | 76 | 82 | 80 | 80 | |
| Crystallization peak temperature/°C | 1029 | 1035 | 1037 | 1020 | 1033 | 1026 | 1030 | |
| Filament strength/MPa | 4141 | 4129 | 4136 | 4147 | 4150 | 4140 | 4143 | |
| Amount of bubbles /pcs | 6 | 8 | 5 | 6 | 5 | 6 | 6 | |
Table 2
| A8 | A9 | A10 | A11 | Traditional E glass | Traditional R glass | Improved R glass | ||
| Component | SiO2 | 58.0 | 60.1 | 59.7 | 60.0 | 54.16 | 60 | 60.75 |
| Al2O3 | 15.1 | 15.4 | 15.7 | 15.2 | 14.32 | 25 | 15.80 | |
| CaO | 15.4 | 14.9 | 15.5 | 15.4 | 22.12 | 9 | 13.90 | |
| MgO | 7.6 | 7.2 | 7.1 | 7.2 | 0.41 | 6 | 7.90 | |
| B2O3 | - | - | - | - | 7.6 | - | - | |
| Na2O | 0.20 | 0.33 | 0.23 | 0.22 | 0.45 | trace amount | 0.73 | |
| K2O | 0.56 | 0.65 | 0.59 | 0.75 | 0.25 | trace amount | ||
| Li2O | 0.30 | 0.30 | 0.19 | 0.25 | 0 | 0 | 0.48 | |
| Fe2O3 | 0.40 | 0.43 | 0.41 | 0.43 | 0.35 | trace amount | 0.18 | |
| TiO2 | 0.34 | 0.39 | 0.38 | 0.35 | 0.34 | trace amount | 0.12 | |
| ZrO2+HfO2 | 2.0 | 0.1 | 0.15 | - | - | - | - | |
| Ratio | C1 | 2.03 | 2.07 | 2.19 | 2.14 | 53.96 | 1.5 | 1.76 |
| C2 | 2.8 | 1.82 | 2.57 | 3.41 | 0.56 | - | - | |
| Parameter | Forming temperature/°C | 1277 | 1277 | 1278 | 1276 | 1175 | 1430 | 1278 |
| Liquidus temperature/°C | 1196 | 1197 | 1200 | 1195 | 1075 | 1350 | 1210 | |
| ΔT/°C | 81 | 80 | 78 | 81 | 100 | 80 | 68 | |
| Crystallization peak temperature/°C | 1032 | 1030 | 1023 | 1034 | / | 1010 | 1016 | |
| Filament strength/MPa | 4164 | 4145 | 4123 | 4149 | 3265 | 4220 | 4089 | |
| Amount of bubbles /pcs | 10 | 5 | 6 | 4 | 3 | 30 | 25 | |
[0058] It can be seen from the values in the above tables that, compared with the traditional R glass and improved R glass, the glass fiber composition of the present invention has the following advantages: (1) Much lower liquidus temperature, which helps to reduce crystallization risk and increases the fiber drawing efficiency. (2) Higher crystallization peak temperature, which means more energy is needed for the crystal nucleuses to form and grow during crystallization procedure, that is to say, the glass of the present invention has lower crystallization risk under the same conditions. (3) Much lower amount of bubbles, which means the fining performance of the molten glass of the present invention is better. Meanwhile, the glass fiber of the present invention has higher filament strength compared with the improved R glass.
[0059] The glass fiber composition according to the present invention can be used for making glass fibers having the aforementioned excellent properties.
[0060] The glass fiber composition according to the present invention can be used in combination with one or more organic and/or inorganic materials for preparing composite materials having excellent performances, such as glass fiber reinforced base materials.
[0061] In conclusion, the present invention provides a boron-free glass fiber composition, glass fiber and composite material therefrom. The composition can not only keep the forming temperature relatively low, but also solve the problems in the production of high-performance glass fiber, such as high liquidus temperature, high crystallization rate, high surface tension, fining difficulty, and the difficulty in efficient and large-scale production. The composition can significantly reduce liquidus temperature and surface tension of molten glass, and reduce crystallization tendency of glass and the amount of bubbles under the same conditions. Meanwhile, the glass fiber made therefrom possesses favorable mechanical strength.
[0062] Finally, what should be made clear is that, in this text, the terms "contain", "comprise" or any other variants are intended to mean "nonexclusively include" so that any process, method, article or equipment that contains a series of factors shall include not only such factors, but also include other factors that are not explicitly listed, or also include intrinsic factors of such process, method, object or equipment. Without more limitations, factors defined by the phrase "contain a..." or its variants do not rule out that there are other same factors in the process, method, article or equipment which include said factors.
[0063] The above examples are provided only for the purpose of illustrating instead of limiting the technical solutions of the present invention. Although the present invention is described in details by way of aforementioned examples, one skilled in the art shall understand that modifications can also be made to the technical solutions embodied by all the aforementioned examples or equivalent replacement can be made to some of the technical features. However, such modifications or replacements will not cause the resulting technical solutions to substantially deviate from the spirits and ranges of the technical solutions respectively embodied by all the examples of the present invention.
INDUSTRIAL APPLICABILITY OF THE INVENTION
[0064] The glass fiber composition of the present invention makes a breakthrough in crystallization properties, filament strength and heat resistance of the glass, as compared with the present mainstream improved R glass, and greatly reduces crystallization risk, and significantly improves the filament strength and softening point temperature under the same conditions; in addition, the cost-performance ratio of the overall technical solutions of said composition is higher, thereby making it more suitable for large-scale industrial production.
1. A boron-free glass fiber composition, wherein, comprising the following components
expressed as percentage by weight:
wherein, the range of the weight percentage ratio C1=CaO/MgO is greater than 2 and
less than or equal to 2.4.
| SiO2 | 58-60.4% |
| Al2O3 | 14-16.5% |
| CaO | 14.1-16.5% |
| MgO | 6-8.2% |
| Li2O | 0.01-0.4% |
| Na2O+K2O | less than 1.15% |
| K2O | greater than 0.5% |
| TiO2 | less than 1.5% |
| Fe2O3 | less than 1% |
2. The boron-free glass fiber composition of claim 1, wherein the range of the weight
percentage ratio C2= K2O/Na2O is greater than 1 and less than or equal to 6.
3. The boron-free glass fiber composition of claim 1, wherein the range of the weight
percentage ratio C1=CaO/MgO is greater than 2 and less than or equal to 2.3.
4. The boron-free glass fiber composition of claim 1, wherein the range of the weight
percentage ratio C2= K2O/Na2O is 1.2-5.
5. The boron-free glass fiber composition of claim 1, wherein, comprising the following
components expressed as percentage by weight:
wherein, the range of the weight percentage ratio C1=CaO/MgO is greater than 2 and
less than or equal to 2.3, the range of the weight percentage ratio C2= K2O/Na2O is greater than 1 and less than or equal to 6.
| SiO2 | 58.5-60.4% |
| Al2O3 | 14.5-16.5% |
| CaO | 14.1-16.1% |
| MgO | 6-8% |
| Li2O | 0.01-0.4% |
| Na2O+K2O | less than 1.15% |
| K2O | greater than 0.5% |
| TiO2 | less than 1.5% |
| Fe2O3 | less than 1% |
6. The boron-free glass fiber composition of claim 1, wherein, comprising the following
components expressed as percentage by weight:
wherein, the range of the weight percentage ratio C1=CaO/MgO is greater than 2 and
less than or equal to 2.14, the range of the weight percentage ratio C2= K2O/Na2O is 1.2-5.
| SiO2 | 58.5-60.4% |
| Al2O3 | 14.5-16.5% |
| CaO | 14.1-16.1% |
| MgO | 6-8% |
| Li2O | 0.01-0.4% |
| Na2O+K2O | less than 1.15% |
| K2O | greater than 0.5% |
| TiO2 | less than 1.5% |
| Fe2O3 | less than 1% |
7. The boron-free glass fiber composition of claim 1 or 6, wherein the content of Li2O expressed as weight percentage is greater than or equal to 0.01 % and less than
0.1 %.
8. The boron-free glass fiber composition of claim 1 or 6, wherein further comprising
ZrO2 and HfO2, and the total content of ZrO2 and HfO2 expressed as weight percentage is 0.01-2%.
9. A glass fiber, wherein, being produced from the glass fiber composition described
in anyone of claims 1 to 8.
10. A composite material, wherein, incorporating the glass fiber described in claim 9.